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\begin{document} |
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|
| 45 |
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|
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\begin{abstract} |
| 47 |
|
|
| 48 |
< |
We have developed a Non-Isotropic Velocity Scaling algorithm for |
| 49 |
< |
setting up and maintaining stable thermal gradients in non-equilibrium |
| 50 |
< |
molecular dynamics simulations. This approach effectively imposes |
| 51 |
< |
unphysical thermal flux even between particles of different |
| 52 |
< |
identities, conserves linear momentum and kinetic energy, and |
| 53 |
< |
minimally perturbs the velocity profile of a system when compared with |
| 54 |
< |
previous RNEMD methods. We have used this method to simulate thermal |
| 55 |
< |
conductance at metal / organic solvent interfaces both with and |
| 56 |
< |
without the presence of thiol-based capping agents. We obtained |
| 57 |
< |
values comparable with experimental values, and observed significant |
| 58 |
< |
conductance enhancement with the presence of capping agents. Computed |
| 59 |
< |
power spectra indicate the acoustic impedance mismatch between metal |
| 60 |
< |
and liquid phase is greatly reduced by the capping agents and thus |
| 61 |
< |
leads to higher interfacial thermal transfer efficiency. |
| 48 |
> |
With the Non-Isotropic Velocity Scaling algorithm (NIVS) we have |
| 49 |
> |
developed, an unphysical thermal flux can be effectively set up even |
| 50 |
> |
for non-homogeneous systems like interfaces in non-equilibrium |
| 51 |
> |
molecular dynamics simulations. In this work, this algorithm is |
| 52 |
> |
applied for simulating thermal conductance at metal / organic solvent |
| 53 |
> |
interfaces with various coverages of butanethiol capping |
| 54 |
> |
agents. Different solvents and force field models were tested. Our |
| 55 |
> |
results suggest that the United-Atom models are able to provide an |
| 56 |
> |
estimate of the interfacial thermal conductivity comparable to |
| 57 |
> |
experiments in our simulations with satisfactory computational |
| 58 |
> |
efficiency. From our results, the acoustic impedance mismatch between |
| 59 |
> |
metal and liquid phase is effectively reduced by the capping |
| 60 |
> |
agents, and thus leads to interfacial thermal conductance |
| 61 |
> |
enhancement. Furthermore, this effect is closely related to the |
| 62 |
> |
capping agent coverage on the metal surfaces and the type of solvent |
| 63 |
> |
molecules, and is affected by the models used in the simulations. |
| 64 |
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|
| 65 |
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\end{abstract} |
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| 73 |
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%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%%% |
| 74 |
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|
| 75 |
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\section{Introduction} |
| 76 |
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[BACKGROUND FOR INTERFACIAL THERMAL CONDUCTANCE PROBLEM] |
| 77 |
< |
Interfacial thermal conductance is extensively studied both |
| 78 |
< |
experimentally and computationally, and systems with interfaces |
| 79 |
< |
present are generally heterogeneous. Although interfaces are commonly |
| 80 |
< |
barriers to heat transfer, it has been |
| 81 |
< |
reported\cite{doi:10.1021/la904855s} that under specific circustances, |
| 82 |
< |
e.g. with certain capping agents present on the surface, interfacial |
| 83 |
< |
conductance can be significantly enhanced. However, heat conductance |
| 82 |
< |
of molecular and nano-scale interfaces will be affected by the |
| 83 |
< |
chemical details of the surface and is challenging to |
| 84 |
< |
experimentalist. The lower thermal flux through interfaces is even |
| 85 |
< |
more difficult to measure with EMD and forward NEMD simulation |
| 86 |
< |
methods. Therefore, developing good simulation methods will be |
| 87 |
< |
desirable in order to investigate thermal transport across interfaces. |
| 76 |
> |
Due to the importance of heat flow in nanotechnology, interfacial |
| 77 |
> |
thermal conductance has been studied extensively both experimentally |
| 78 |
> |
and computationally.\cite{cahill:793} Unlike bulk materials, nanoscale |
| 79 |
> |
materials have a significant fraction of their atoms at interfaces, |
| 80 |
> |
and the chemical details of these interfaces govern the heat transfer |
| 81 |
> |
behavior. Furthermore, the interfaces are |
| 82 |
> |
heterogeneous (e.g. solid - liquid), which provides a challenge to |
| 83 |
> |
traditional methods developed for homogeneous systems. |
| 84 |
|
|
| 85 |
< |
Recently, we have developed the Non-Isotropic Velocity Scaling (NIVS) |
| 85 |
> |
Experimentally, various interfaces have been investigated for their |
| 86 |
> |
thermal conductance. Cahill and coworkers studied nanoscale thermal |
| 87 |
> |
transport from metal nanoparticle/fluid interfaces, to epitaxial |
| 88 |
> |
TiN/single crystal oxides interfaces, to hydrophilic and hydrophobic |
| 89 |
> |
interfaces between water and solids with different self-assembled |
| 90 |
> |
monolayers.\cite{Wilson:2002uq,PhysRevB.67.054302,doi:10.1021/jp048375k,PhysRevLett.96.186101} |
| 91 |
> |
Wang {\it et al.} studied heat transport through |
| 92 |
> |
long-chain hydrocarbon monolayers on gold substrate at individual |
| 93 |
> |
molecular level,\cite{Wang10082007} Schmidt {\it et al.} studied the |
| 94 |
> |
role of CTAB on thermal transport between gold nanorods and |
| 95 |
> |
solvent,\cite{doi:10.1021/jp8051888} and Juv\'e {\it et al.} studied |
| 96 |
> |
the cooling dynamics, which is controlled by thermal interface |
| 97 |
> |
resistence of glass-embedded metal |
| 98 |
> |
nanoparticles.\cite{PhysRevB.80.195406} Although interfaces are |
| 99 |
> |
normally considered barriers for heat transport, Alper {\it et al.} |
| 100 |
> |
suggested that specific ligands (capping agents) could completely |
| 101 |
> |
eliminate this barrier |
| 102 |
> |
($G\rightarrow\infty$).\cite{doi:10.1021/la904855s} |
| 103 |
> |
|
| 104 |
> |
Theoretical and computational models have also been used to study the |
| 105 |
> |
interfacial thermal transport in order to gain an understanding of |
| 106 |
> |
this phenomena at the molecular level. Recently, Hase and coworkers |
| 107 |
> |
employed Non-Equilibrium Molecular Dynamics (NEMD) simulations to |
| 108 |
> |
study thermal transport from hot Au(111) substrate to a self-assembled |
| 109 |
> |
monolayer of alkylthiol with relatively long chain (8-20 carbon |
| 110 |
> |
atoms).\cite{hase:2010,hase:2011} However, ensemble averaged |
| 111 |
> |
measurements for heat conductance of interfaces between the capping |
| 112 |
> |
monolayer on Au and a solvent phase have yet to be studied with their |
| 113 |
> |
approach. The comparatively low thermal flux through interfaces is |
| 114 |
> |
difficult to measure with Equilibrium |
| 115 |
> |
MD\cite{doi:10.1080/0026897031000068578} or forward NEMD simulation |
| 116 |
> |
methods. Therefore, the Reverse NEMD (RNEMD) |
| 117 |
> |
methods\cite{MullerPlathe:1997xw,kuang:164101} would have the |
| 118 |
> |
advantage of applying this difficult to measure flux (while measuring |
| 119 |
> |
the resulting gradient), given that the simulation methods being able |
| 120 |
> |
to effectively apply an unphysical flux in non-homogeneous systems. |
| 121 |
> |
Garde and coworkers\cite{garde:nl2005,garde:PhysRevLett2009} applied |
| 122 |
> |
this approach to various liquid interfaces and studied how thermal |
| 123 |
> |
conductance (or resistance) is dependent on chemistry details of |
| 124 |
> |
interfaces, e.g. hydrophobic and hydrophilic aqueous interfaces. |
| 125 |
> |
|
| 126 |
> |
Recently, we have developed a Non-Isotropic Velocity Scaling (NIVS) |
| 127 |
|
algorithm for RNEMD simulations\cite{kuang:164101}. This algorithm |
| 128 |
|
retains the desirable features of RNEMD (conservation of linear |
| 129 |
|
momentum and total energy, compatibility with periodic boundary |
| 130 |
|
conditions) while establishing true thermal distributions in each of |
| 131 |
< |
the two slabs. Furthermore, it allows more effective thermal exchange |
| 132 |
< |
between particles of different identities, and thus enables extensive |
| 133 |
< |
study of interfacial conductance. |
| 131 |
> |
the two slabs. Furthermore, it allows effective thermal exchange |
| 132 |
> |
between particles of different identities, and thus makes the study of |
| 133 |
> |
interfacial conductance much simpler. |
| 134 |
|
|
| 135 |
+ |
The work presented here deals with the Au(111) surface covered to |
| 136 |
+ |
varying degrees by butanethiol, a capping agent with short carbon |
| 137 |
+ |
chain, and solvated with organic solvents of different molecular |
| 138 |
+ |
properties. Different models were used for both the capping agent and |
| 139 |
+ |
the solvent force field parameters. Using the NIVS algorithm, the |
| 140 |
+ |
thermal transport across these interfaces was studied and the |
| 141 |
+ |
underlying mechanism for the phenomena was investigated. |
| 142 |
+ |
|
| 143 |
|
\section{Methodology} |
| 144 |
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\subsection{Algorithm} |
| 145 |
< |
[BACKGROUND FOR MD METHODS] |
| 146 |
< |
There have been many algorithms for computing thermal conductivity |
| 147 |
< |
using molecular dynamics simulations. However, interfacial conductance |
| 148 |
< |
is at least an order of magnitude smaller. This would make the |
| 149 |
< |
calculation even more difficult for those slowly-converging |
| 150 |
< |
equilibrium methods. Imposed-flux non-equilibrium |
| 151 |
< |
methods\cite{MullerPlathe:1997xw} have the flux set {\it a priori} and |
| 152 |
< |
the response of temperature or momentum gradients are easier to |
| 153 |
< |
measure than the flux, if unknown, and thus, is a preferable way to |
| 154 |
< |
the forward NEMD methods. Although the momentum swapping approach for |
| 155 |
< |
flux-imposing can be used for exchanging energy between particles of |
| 156 |
< |
different identity, the kinetic energy transfer efficiency is affected |
| 157 |
< |
by the mass difference between the particles, which limits its |
| 158 |
< |
application on heterogeneous interfacial systems. |
| 144 |
> |
\subsection{Imposd-Flux Methods in MD Simulations} |
| 145 |
> |
Steady state MD simulations have an advantage in that not many |
| 146 |
> |
trajectories are needed to study the relationship between thermal flux |
| 147 |
> |
and thermal gradients. For systems with low interfacial conductance, |
| 148 |
> |
one must have a method capable of generating or measuring relatively |
| 149 |
> |
small fluxes, compared to those required for bulk conductivity. This |
| 150 |
> |
requirement makes the calculation even more difficult for |
| 151 |
> |
slowly-converging equilibrium methods.\cite{Viscardy:2007lq} Forward |
| 152 |
> |
NEMD methods impose a gradient (and measure a flux), but at interfaces |
| 153 |
> |
it is not clear what behavior should be imposed at the boundaries |
| 154 |
> |
between materials. Imposed-flux reverse non-equilibrium |
| 155 |
> |
methods\cite{MullerPlathe:1997xw} set the flux {\it a priori} and |
| 156 |
> |
the thermal response becomes an easy-to-measure quantity. Although |
| 157 |
> |
M\"{u}ller-Plathe's original momentum swapping approach can be used |
| 158 |
> |
for exchanging energy between particles of different identity, the |
| 159 |
> |
kinetic energy transfer efficiency is affected by the mass difference |
| 160 |
> |
between the particles, which limits its application on heterogeneous |
| 161 |
> |
interfacial systems. |
| 162 |
|
|
| 163 |
< |
The non-isotropic velocity scaling (NIVS)\cite{kuang:164101} approach in |
| 164 |
< |
non-equilibrium MD simulations is able to impose relatively large |
| 165 |
< |
kinetic energy flux without obvious perturbation to the velocity |
| 166 |
< |
distribution of the simulated systems. Furthermore, this approach has |
| 163 |
> |
The non-isotropic velocity scaling (NIVS) \cite{kuang:164101} approach |
| 164 |
> |
to non-equilibrium MD simulations is able to impose a wide range of |
| 165 |
> |
kinetic energy fluxes without obvious perturbation to the velocity |
| 166 |
> |
distributions of the simulated systems. Furthermore, this approach has |
| 167 |
|
the advantage in heterogeneous interfaces in that kinetic energy flux |
| 168 |
|
can be applied between regions of particles of arbitary identity, and |
| 169 |
< |
the flux quantity is not restricted by particle mass difference. |
| 169 |
> |
the flux will not be restricted by difference in particle mass. |
| 170 |
|
|
| 171 |
|
The NIVS algorithm scales the velocity vectors in two separate regions |
| 172 |
|
of a simulation system with respective diagonal scaling matricies. To |
| 173 |
|
determine these scaling factors in the matricies, a set of equations |
| 174 |
|
including linear momentum conservation and kinetic energy conservation |
| 175 |
< |
constraints and target momentum/energy flux satisfaction is |
| 176 |
< |
solved. With the scaling operation applied to the system in a set |
| 177 |
< |
frequency, corresponding momentum/temperature gradients can be built, |
| 178 |
< |
which can be used for computing transportation properties and other |
| 179 |
< |
applications related to momentum/temperature gradients. The NIVS |
| 132 |
< |
algorithm conserves momenta and energy and does not depend on an |
| 133 |
< |
external thermostat. |
| 175 |
> |
constraints and target energy flux satisfaction is solved. With the |
| 176 |
> |
scaling operation applied to the system in a set frequency, bulk |
| 177 |
> |
temperature gradients can be easily established, and these can be used |
| 178 |
> |
for computing thermal conductivities. The NIVS algorithm conserves |
| 179 |
> |
momenta and energy and does not depend on an external thermostat. |
| 180 |
|
|
| 181 |
< |
\subsection{Defining Interfacial Thermal Conductivity $G$} |
| 182 |
< |
For interfaces with a relatively low interfacial conductance, the bulk |
| 183 |
< |
regions on either side of an interface rapidly come to a state in |
| 184 |
< |
which the two phases have relatively homogeneous (but distinct) |
| 185 |
< |
temperatures. The interfacial thermal conductivity $G$ can therefore |
| 186 |
< |
be approximated as: |
| 181 |
> |
\subsection{Defining Interfacial Thermal Conductivity ($G$)} |
| 182 |
> |
|
| 183 |
> |
For an interface with relatively low interfacial conductance, and a |
| 184 |
> |
thermal flux between two distinct bulk regions, the regions on either |
| 185 |
> |
side of the interface rapidly come to a state in which the two phases |
| 186 |
> |
have relatively homogeneous (but distinct) temperatures. The |
| 187 |
> |
interfacial thermal conductivity $G$ can therefore be approximated as: |
| 188 |
|
\begin{equation} |
| 189 |
< |
G = \frac{E_{total}}{2 t L_x L_y \left( \langle T_\mathrm{hot}\rangle - |
| 189 |
> |
G = \frac{E_{total}}{2 t L_x L_y \left( \langle T_\mathrm{hot}\rangle - |
| 190 |
|
\langle T_\mathrm{cold}\rangle \right)} |
| 191 |
|
\label{lowG} |
| 192 |
|
\end{equation} |
| 193 |
< |
where ${E_{total}}$ is the imposed non-physical kinetic energy |
| 194 |
< |
transfer and ${\langle T_\mathrm{hot}\rangle}$ and ${\langle |
| 195 |
< |
T_\mathrm{cold}\rangle}$ are the average observed temperature of the |
| 196 |
< |
two separated phases. |
| 193 |
> |
where ${E_{total}}$ is the total imposed non-physical kinetic energy |
| 194 |
> |
transfer during the simulation and ${\langle T_\mathrm{hot}\rangle}$ |
| 195 |
> |
and ${\langle T_\mathrm{cold}\rangle}$ are the average observed |
| 196 |
> |
temperature of the two separated phases. For an applied flux $J_z$ |
| 197 |
> |
operating over a simulation time $t$ on a periodically-replicated slab |
| 198 |
> |
of dimensions $L_x \times L_y$, $E_{total} = J_z *(t)*(2 L_x L_y)$. |
| 199 |
|
|
| 200 |
< |
When the interfacial conductance is {\it not} small, two ways can be |
| 201 |
< |
used to define $G$. |
| 202 |
< |
|
| 203 |
< |
One way is to assume the temperature is discretely different on two |
| 204 |
< |
sides of the interface, $G$ can be calculated with the thermal flux |
| 205 |
< |
applied $J$ and the maximum temperature difference measured along the |
| 206 |
< |
thermal gradient max($\Delta T$), which occurs at the interface, as: |
| 200 |
> |
When the interfacial conductance is {\it not} small, there are two |
| 201 |
> |
ways to define $G$. One common way is to assume the temperature is |
| 202 |
> |
discrete on the two sides of the interface. $G$ can be calculated |
| 203 |
> |
using the applied thermal flux $J$ and the maximum temperature |
| 204 |
> |
difference measured along the thermal gradient max($\Delta T$), which |
| 205 |
> |
occurs at the Gibbs deviding surface (Figure \ref{demoPic}). This is |
| 206 |
> |
known as the Kapitza conductance, which is the inverse of the Kapitza |
| 207 |
> |
resistance. |
| 208 |
|
\begin{equation} |
| 209 |
< |
G=\frac{J}{\Delta T} |
| 209 |
> |
G=\frac{J}{\Delta T} |
| 210 |
|
\label{discreteG} |
| 211 |
|
\end{equation} |
| 212 |
|
|
| 213 |
+ |
\begin{figure} |
| 214 |
+ |
\includegraphics[width=\linewidth]{method} |
| 215 |
+ |
\caption{Interfacial conductance can be calculated by applying an |
| 216 |
+ |
(unphysical) kinetic energy flux between two slabs, one located |
| 217 |
+ |
within the metal and another on the edge of the periodic box. The |
| 218 |
+ |
system responds by forming a thermal response or a gradient. In |
| 219 |
+ |
bulk liquids, this gradient typically has a single slope, but in |
| 220 |
+ |
interfacial systems, there are distinct thermal conductivity |
| 221 |
+ |
domains. The interfacial conductance, $G$ is found by measuring the |
| 222 |
+ |
temperature gap at the Gibbs dividing surface, or by using second |
| 223 |
+ |
derivatives of the thermal profile.} |
| 224 |
+ |
\label{demoPic} |
| 225 |
+ |
\end{figure} |
| 226 |
+ |
|
| 227 |
|
The other approach is to assume a continuous temperature profile along |
| 228 |
|
the thermal gradient axis (e.g. $z$) and define $G$ at the point where |
| 229 |
< |
the magnitude of thermal conductivity $\lambda$ change reach its |
| 229 |
> |
the magnitude of thermal conductivity ($\lambda$) change reaches its |
| 230 |
|
maximum, given that $\lambda$ is well-defined throughout the space: |
| 231 |
|
\begin{equation} |
| 232 |
|
G^\prime = \Big|\frac{\partial\lambda}{\partial z}\Big| |
| 237 |
|
\label{derivativeG} |
| 238 |
|
\end{equation} |
| 239 |
|
|
| 240 |
< |
With the temperature profile obtained from simulations, one is able to |
| 240 |
> |
With temperature profiles obtained from simulation, one is able to |
| 241 |
|
approximate the first and second derivatives of $T$ with finite |
| 242 |
< |
difference method and thus calculate $G^\prime$. |
| 242 |
> |
difference methods and calculate $G^\prime$. In what follows, both |
| 243 |
> |
definitions have been used, and are compared in the results. |
| 244 |
|
|
| 245 |
< |
In what follows, both definitions are used for calculation and comparison. |
| 245 |
> |
To investigate the interfacial conductivity at metal / solvent |
| 246 |
> |
interfaces, we have modeled a metal slab with its (111) surfaces |
| 247 |
> |
perpendicular to the $z$-axis of our simulation cells. The metal slab |
| 248 |
> |
has been prepared both with and without capping agents on the exposed |
| 249 |
> |
surface, and has been solvated with simple organic solvents, as |
| 250 |
> |
illustrated in Figure \ref{gradT}. |
| 251 |
|
|
| 252 |
< |
[IMPOSE G DEFINITION INTO OUR SYSTEMS] |
| 253 |
< |
To facilitate the use of the above definitions in calculating $G$ and |
| 254 |
< |
$G^\prime$, we have a metal slab with its (111) surfaces perpendicular |
| 255 |
< |
to the $z$-axis of our simulation cells. With or withour capping |
| 256 |
< |
agents on the surfaces, the metal slab is solvated with organic |
| 257 |
< |
solvents, as illustrated in Figure \ref{demoPic}. |
| 252 |
> |
With the simulation cell described above, we are able to equilibrate |
| 253 |
> |
the system and impose an unphysical thermal flux between the liquid |
| 254 |
> |
and the metal phase using the NIVS algorithm. By periodically applying |
| 255 |
> |
the unphysical flux, we obtained a temperature profile and its spatial |
| 256 |
> |
derivatives. Figure \ref{gradT} shows how an applied thermal flux can |
| 257 |
> |
be used to obtain the 1st and 2nd derivatives of the temperature |
| 258 |
> |
profile. |
| 259 |
|
|
| 260 |
|
\begin{figure} |
| 190 |
– |
\includegraphics[width=\linewidth]{demoPic} |
| 191 |
– |
\caption{A sample showing how a metal slab has its (111) surface |
| 192 |
– |
covered by capping agent molecules and solvated by hexane.} |
| 193 |
– |
\label{demoPic} |
| 194 |
– |
\end{figure} |
| 195 |
– |
|
| 196 |
– |
With a simulation cell setup following the above manner, one is able |
| 197 |
– |
to equilibrate the system and impose an unphysical thermal flux |
| 198 |
– |
between the liquid and the metal phase with the NIVS algorithm. Under |
| 199 |
– |
a stablized thermal gradient induced by periodically applying the |
| 200 |
– |
unphysical flux, one is able to obtain a temperature profile and the |
| 201 |
– |
physical thermal flux corresponding to it, which equals to the |
| 202 |
– |
unphysical flux applied by NIVS. These data enables the evaluation of |
| 203 |
– |
the interfacial thermal conductance of a surface. Figure \ref{gradT} |
| 204 |
– |
is an example how those stablized thermal gradient can be used to |
| 205 |
– |
obtain the 1st and 2nd derivatives of the temperature profile. |
| 206 |
– |
|
| 207 |
– |
\begin{figure} |
| 261 |
|
\includegraphics[width=\linewidth]{gradT} |
| 262 |
< |
\caption{The 1st and 2nd derivatives of temperature profile can be |
| 263 |
< |
obtained with finite difference approximation.} |
| 262 |
> |
\caption{A sample of Au-butanethiol/hexane interfacial system and the |
| 263 |
> |
temperature profile after a kinetic energy flux is imposed to |
| 264 |
> |
it. The 1st and 2nd derivatives of the temperature profile can be |
| 265 |
> |
obtained with finite difference approximation (lower panel).} |
| 266 |
|
\label{gradT} |
| 267 |
|
\end{figure} |
| 268 |
|
|
| 269 |
|
\section{Computational Details} |
| 270 |
< |
\subsection{System Geometry} |
| 271 |
< |
In our simulations, Au is used to construct a metal slab with bare |
| 272 |
< |
(111) surface perpendicular to the $z$-axis. Different slab thickness |
| 273 |
< |
(layer numbers of Au) are simulated. This metal slab is first |
| 274 |
< |
equilibrated under normal pressure (1 atm) and a desired |
| 275 |
< |
temperature. After equilibration, butanethiol is used as the capping |
| 276 |
< |
agent molecule to cover the bare Au (111) surfaces evenly. The sulfur |
| 277 |
< |
atoms in the butanethiol molecules would occupy the three-fold sites |
| 278 |
< |
of the surfaces, and the maximal butanethiol capacity on Au surface is |
| 279 |
< |
$1/3$ of the total number of surface Au atoms[CITATION]. A series of |
| 280 |
< |
different coverage surfaces is investigated in order to study the |
| 281 |
< |
relation between coverage and conductance. |
| 282 |
< |
|
| 283 |
< |
[COVERAGE DISCRIPTION] However, since the interactions between surface |
| 284 |
< |
Au and butanethiol is non-bonded, the capping agent molecules are |
| 285 |
< |
allowed to migrate to an empty neighbor three-fold site during a |
| 286 |
< |
simulation. Therefore, the initial configuration would not severely |
| 232 |
< |
affect the sampling of a variety of configurations of the same |
| 233 |
< |
coverage, and the final conductance measurement would be an average |
| 234 |
< |
effect of these configurations explored in the simulations. [MAY NEED FIGURES] |
| 270 |
> |
\subsection{Simulation Protocol} |
| 271 |
> |
The NIVS algorithm has been implemented in our MD simulation code, |
| 272 |
> |
OpenMD\cite{Meineke:2005gd,openmd}, and was used for our simulations. |
| 273 |
> |
Metal slabs of 6 or 11 layers of Au atoms were first equilibrated |
| 274 |
> |
under atmospheric pressure (1 atm) and 200K. After equilibration, |
| 275 |
> |
butanethiol capping agents were placed at three-fold hollow sites on |
| 276 |
> |
the Au(111) surfaces. These sites are either {\it fcc} or {\it |
| 277 |
> |
hcp} sites, although Hase {\it et al.} found that they are |
| 278 |
> |
equivalent in a heat transfer process,\cite{hase:2010} so we did not |
| 279 |
> |
distinguish between these sites in our study. The maximum butanethiol |
| 280 |
> |
capacity on Au surface is $1/3$ of the total number of surface Au |
| 281 |
> |
atoms, and the packing forms a $(\sqrt{3}\times\sqrt{3})R30^\circ$ |
| 282 |
> |
structure\cite{doi:10.1021/ja00008a001,doi:10.1021/cr9801317}. A |
| 283 |
> |
series of lower coverages was also prepared by eliminating |
| 284 |
> |
butanethiols from the higher coverage surface in a regular manner. The |
| 285 |
> |
lower coverages were prepared in order to study the relation between |
| 286 |
> |
coverage and interfacial conductance. |
| 287 |
|
|
| 288 |
< |
After the modified Au-butanethiol surface systems are equilibrated |
| 289 |
< |
under canonical ensemble, Packmol\cite{packmol} is used to pack |
| 290 |
< |
organic solvent molecules in the previously vacuum part of the |
| 291 |
< |
simulation cells, which guarantees that short range repulsive |
| 292 |
< |
interactions do not disrupt the simulations. Two solvents are |
| 293 |
< |
investigated, one which has little vibrational overlap with the |
| 294 |
< |
alkanethiol and plane-like shape (toluene), and one which has similar |
| 243 |
< |
vibrational frequencies and chain-like shape ({\it n}-hexane). The |
| 244 |
< |
spacing filled by solvent molecules, i.e. the gap between periodically |
| 245 |
< |
repeated Au-butanethiol surfaces should be carefully chosen so that it |
| 246 |
< |
would not be too short to affect the liquid phase structure, nor too |
| 247 |
< |
long, leading to over cooling (freezing) or heating (boiling) when a |
| 248 |
< |
thermal flux is applied. In our simulations, this spacing is usually |
| 249 |
< |
$35 \sim 60$\AA. |
| 288 |
> |
The capping agent molecules were allowed to migrate during the |
| 289 |
> |
simulations. They distributed themselves uniformly and sampled a |
| 290 |
> |
number of three-fold sites throughout out study. Therefore, the |
| 291 |
> |
initial configuration does not noticeably affect the sampling of a |
| 292 |
> |
variety of configurations of the same coverage, and the final |
| 293 |
> |
conductance measurement would be an average effect of these |
| 294 |
> |
configurations explored in the simulations. |
| 295 |
|
|
| 296 |
< |
The initial configurations generated by Packmol are further |
| 297 |
< |
equilibrated with the $x$ and $y$ dimensions fixed, only allowing |
| 298 |
< |
length scale change in $z$ dimension. This is to ensure that the |
| 299 |
< |
equilibration of liquid phase does not affect the metal crystal |
| 300 |
< |
structure in $x$ and $y$ dimensions. Further equilibration are run |
| 301 |
< |
under NVT and then NVE ensembles. |
| 296 |
> |
After the modified Au-butanethiol surface systems were equilibrated in |
| 297 |
> |
the canonical (NVT) ensemble, organic solvent molecules were packed in |
| 298 |
> |
the previously empty part of the simulation cells.\cite{packmol} Two |
| 299 |
> |
solvents were investigated, one which has little vibrational overlap |
| 300 |
> |
with the alkanethiol and which has a planar shape (toluene), and one |
| 301 |
> |
which has similar vibrational frequencies to the capping agent and |
| 302 |
> |
chain-like shape ({\it n}-hexane). |
| 303 |
|
|
| 304 |
< |
After the systems reach equilibrium, NIVS is implemented to impose a |
| 305 |
< |
periodic unphysical thermal flux between the metal and the liquid |
| 306 |
< |
phase. Most of our simulations are under an average temperature of |
| 307 |
< |
$\sim$200K. Therefore, this flux usually comes from the metal to the |
| 304 |
> |
The simulation cells were not particularly extensive along the |
| 305 |
> |
$z$-axis, as a very long length scale for the thermal gradient may |
| 306 |
> |
cause excessively hot or cold temperatures in the middle of the |
| 307 |
> |
solvent region and lead to undesired phenomena such as solvent boiling |
| 308 |
> |
or freezing when a thermal flux is applied. Conversely, too few |
| 309 |
> |
solvent molecules would change the normal behavior of the liquid |
| 310 |
> |
phase. Therefore, our $N_{solvent}$ values were chosen to ensure that |
| 311 |
> |
these extreme cases did not happen to our simulations. The spacing |
| 312 |
> |
between periodic images of the gold interfaces is $45 \sim 75$\AA. |
| 313 |
> |
|
| 314 |
> |
The initial configurations generated are further equilibrated with the |
| 315 |
> |
$x$ and $y$ dimensions fixed, only allowing the $z$-length scale to |
| 316 |
> |
change. This is to ensure that the equilibration of liquid phase does |
| 317 |
> |
not affect the metal's crystalline structure. Comparisons were made |
| 318 |
> |
with simulations that allowed changes of $L_x$ and $L_y$ during NPT |
| 319 |
> |
equilibration. No substantial changes in the box geometry were noticed |
| 320 |
> |
in these simulations. After ensuring the liquid phase reaches |
| 321 |
> |
equilibrium at atmospheric pressure (1 atm), further equilibration was |
| 322 |
> |
carried out under canonical (NVT) and microcanonical (NVE) ensembles. |
| 323 |
> |
|
| 324 |
> |
After the systems reach equilibrium, NIVS was used to impose an |
| 325 |
> |
unphysical thermal flux between the metal and the liquid phases. Most |
| 326 |
> |
of our simulations were done under an average temperature of |
| 327 |
> |
$\sim$200K. Therefore, thermal flux usually came from the metal to the |
| 328 |
|
liquid so that the liquid has a higher temperature and would not |
| 329 |
< |
freeze due to excessively low temperature. This induced temperature |
| 330 |
< |
gradient is stablized and the simulation cell is devided evenly into |
| 331 |
< |
N slabs along the $z$-axis and the temperatures of each slab are |
| 332 |
< |
recorded. When the slab width $d$ of each slab is the same, the |
| 333 |
< |
derivatives of $T$ with respect to slab number $n$ can be directly |
| 334 |
< |
used for $G^\prime$ calculations: |
| 335 |
< |
\begin{equation} |
| 336 |
< |
G^\prime = |J_z|\Big|\frac{\partial^2 T}{\partial z^2}\Big| |
| 329 |
> |
freeze due to lowered temperatures. After this induced temperature |
| 330 |
> |
gradient had stablized, the temperature profile of the simulation cell |
| 331 |
> |
was recorded. To do this, the simulation cell is devided evenly into |
| 332 |
> |
$N$ slabs along the $z$-axis. The average temperatures of each slab |
| 333 |
> |
are recorded for 1$\sim$2 ns. When the slab width $d$ of each slab is |
| 334 |
> |
the same, the derivatives of $T$ with respect to slab number $n$ can |
| 335 |
> |
be directly used for $G^\prime$ calculations: \begin{equation} |
| 336 |
> |
G^\prime = |J_z|\Big|\frac{\partial^2 T}{\partial z^2}\Big| |
| 337 |
|
\Big/\left(\frac{\partial T}{\partial z}\right)^2 |
| 338 |
|
= |J_z|\Big|\frac{1}{d^2}\frac{\partial^2 T}{\partial n^2}\Big| |
| 339 |
|
\Big/\left(\frac{1}{d}\frac{\partial T}{\partial n}\right)^2 |
| 342 |
|
\label{derivativeG2} |
| 343 |
|
\end{equation} |
| 344 |
|
|
| 345 |
+ |
All of the above simulation procedures use a time step of 1 fs. Each |
| 346 |
+ |
equilibration stage took a minimum of 100 ps, although in some cases, |
| 347 |
+ |
longer equilibration stages were utilized. |
| 348 |
+ |
|
| 349 |
|
\subsection{Force Field Parameters} |
| 350 |
< |
Our simulations include various components. Therefore, force field |
| 351 |
< |
parameter descriptions are needed for interactions both between the |
| 352 |
< |
same type of particles and between particles of different species. |
| 350 |
> |
Our simulations include a number of chemically distinct components. |
| 351 |
> |
Figure \ref{demoMol} demonstrates the sites defined for both |
| 352 |
> |
United-Atom and All-Atom models of the organic solvent and capping |
| 353 |
> |
agents in our simulations. Force field parameters are needed for |
| 354 |
> |
interactions both between the same type of particles and between |
| 355 |
> |
particles of different species. |
| 356 |
|
|
| 357 |
+ |
\begin{figure} |
| 358 |
+ |
\includegraphics[width=\linewidth]{structures} |
| 359 |
+ |
\caption{Structures of the capping agent and solvents utilized in |
| 360 |
+ |
these simulations. The chemically-distinct sites (a-e) are expanded |
| 361 |
+ |
in terms of constituent atoms for both United Atom (UA) and All Atom |
| 362 |
+ |
(AA) force fields. Most parameters are from |
| 363 |
+ |
Refs. \protect\cite{TraPPE-UA.alkanes,TraPPE-UA.alkylbenzenes,TraPPE-UA.thiols} |
| 364 |
+ |
(UA) and \protect\cite{OPLSAA} (AA). Cross-interactions with the Au |
| 365 |
+ |
atoms are given in Table \ref{MnM}.} |
| 366 |
+ |
\label{demoMol} |
| 367 |
+ |
\end{figure} |
| 368 |
+ |
|
| 369 |
|
The Au-Au interactions in metal lattice slab is described by the |
| 370 |
|
quantum Sutton-Chen (QSC) formulation.\cite{PhysRevB.59.3527} The QSC |
| 371 |
|
potentials include zero-point quantum corrections and are |
| 372 |
|
reparametrized for accurate surface energies compared to the |
| 373 |
< |
Sutton-Chen potentials\cite{Chen90}. |
| 373 |
> |
Sutton-Chen potentials.\cite{Chen90} |
| 374 |
|
|
| 375 |
< |
For both solvent molecules, straight chain {\it n}-hexane and aromatic |
| 376 |
< |
toluene, United-Atom (UA) and All-Atom (AA) models are used |
| 377 |
< |
respectively. The TraPPE-UA |
| 375 |
> |
For the two solvent molecules, {\it n}-hexane and toluene, two |
| 376 |
> |
different atomistic models were utilized. Both solvents were modeled |
| 377 |
> |
using United-Atom (UA) and All-Atom (AA) models. The TraPPE-UA |
| 378 |
|
parameters\cite{TraPPE-UA.alkanes,TraPPE-UA.alkylbenzenes} are used |
| 379 |
< |
for our UA solvent molecules. In these models, pseudo-atoms are |
| 380 |
< |
located at the carbon centers for alkyl groups. By eliminating |
| 381 |
< |
explicit hydrogen atoms, these models are simple and computationally |
| 382 |
< |
efficient, while maintains good accuracy. [LOW BOILING POINT IS A |
| 383 |
< |
KNOWN PROBLEM FOR TRAPPE-UA ALKANES, NEED MORE DISCUSSION] |
| 299 |
< |
for |
| 300 |
< |
toluene, force fields are |
| 301 |
< |
used with rigid body constraints applied.[MORE DETAILS NEEDED] |
| 379 |
> |
for our UA solvent molecules. In these models, sites are located at |
| 380 |
> |
the carbon centers for alkyl groups. Bonding interactions, including |
| 381 |
> |
bond stretches and bends and torsions, were used for intra-molecular |
| 382 |
> |
sites closer than 3 bonds. For non-bonded interactions, Lennard-Jones |
| 383 |
> |
potentials are used. |
| 384 |
|
|
| 385 |
< |
Besides the TraPPE-UA models, AA models are included in our studies as |
| 386 |
< |
well. For hexane, the OPLS all-atom\cite{OPLSAA} force field is |
| 387 |
< |
used. [MORE DETAILS] |
| 388 |
< |
For toluene, |
| 385 |
> |
By eliminating explicit hydrogen atoms, the TraPPE-UA models are |
| 386 |
> |
simple and computationally efficient, while maintaining good accuracy. |
| 387 |
> |
However, the TraPPE-UA model for alkanes is known to predict a slighly |
| 388 |
> |
lower boiling point than experimental values. This is one of the |
| 389 |
> |
reasons we used a lower average temperature (200K) for our |
| 390 |
> |
simulations. If heat is transferred to the liquid phase during the |
| 391 |
> |
NIVS simulation, the liquid in the hot slab can actually be |
| 392 |
> |
substantially warmer than the mean temperature in the simulation. The |
| 393 |
> |
lower mean temperatures therefore prevent solvent boiling. |
| 394 |
|
|
| 395 |
< |
Buatnethiol molecules are used as capping agent for some of our |
| 396 |
< |
simulations. United-Atom\cite{TraPPE-UA.thiols} and All-Atom models |
| 397 |
< |
are respectively used corresponding to the force field type of |
| 398 |
< |
solvent. |
| 395 |
> |
For UA-toluene, the non-bonded potentials between intermolecular sites |
| 396 |
> |
have a similar Lennard-Jones formulation. The toluene molecules were |
| 397 |
> |
treated as a single rigid body, so there was no need for |
| 398 |
> |
intramolecular interactions (including bonds, bends, or torsions) in |
| 399 |
> |
this solvent model. |
| 400 |
|
|
| 401 |
< |
To describe the interactions between metal Au and non-metal capping |
| 402 |
< |
agent and solvent, we refer to Vlugt\cite{vlugt:cpc2007154} and derive |
| 403 |
< |
other interactions which are not parametrized in their work. (can add |
| 404 |
< |
hautman and klein's paper here and more discussion; need to put |
| 405 |
< |
aromatic-metal interaction approximation here) |
| 401 |
> |
Besides the TraPPE-UA models, AA models for both organic solvents are |
| 402 |
> |
included in our studies as well. The OPLS-AA\cite{OPLSAA} force fields |
| 403 |
> |
were used. For hexane, additional explicit hydrogen sites were |
| 404 |
> |
included. Besides bonding and non-bonded site-site interactions, |
| 405 |
> |
partial charges and the electrostatic interactions were added to each |
| 406 |
> |
CT and HC site. For toluene, a flexible model for the toluene molecule |
| 407 |
> |
was utilized which included bond, bend, torsion, and inversion |
| 408 |
> |
potentials to enforce ring planarity. |
| 409 |
|
|
| 410 |
< |
[TABULATED FORCE FIELD PARAMETERS NEEDED] |
| 410 |
> |
The butanethiol capping agent in our simulations, were also modeled |
| 411 |
> |
with both UA and AA model. The TraPPE-UA force field includes |
| 412 |
> |
parameters for thiol molecules\cite{TraPPE-UA.thiols} and are used for |
| 413 |
> |
UA butanethiol model in our simulations. The OPLS-AA also provides |
| 414 |
> |
parameters for alkyl thiols. However, alkyl thiols adsorbed on Au(111) |
| 415 |
> |
surfaces do not have the hydrogen atom bonded to sulfur. To derive |
| 416 |
> |
suitable parameters for butanethiol adsorbed on Au(111) surfaces, we |
| 417 |
> |
adopt the S parameters from Luedtke and Landman\cite{landman:1998} and |
| 418 |
> |
modify the parameters for the CTS atom to maintain charge neutrality |
| 419 |
> |
in the molecule. Note that the model choice (UA or AA) for the capping |
| 420 |
> |
agent can be different from the solvent. Regardless of model choice, |
| 421 |
> |
the force field parameters for interactions between capping agent and |
| 422 |
> |
solvent can be derived using Lorentz-Berthelot Mixing Rule: |
| 423 |
> |
\begin{eqnarray} |
| 424 |
> |
\sigma_{ij} & = & \frac{1}{2} \left(\sigma_{ii} + \sigma_{jj}\right) \\ |
| 425 |
> |
\epsilon_{ij} & = & \sqrt{\epsilon_{ii}\epsilon_{jj}} |
| 426 |
> |
\end{eqnarray} |
| 427 |
|
|
| 428 |
< |
\section{Results} |
| 429 |
< |
\subsection{Toluene Solvent} |
| 428 |
> |
To describe the interactions between metal (Au) and non-metal atoms, |
| 429 |
> |
we refer to an adsorption study of alkyl thiols on gold surfaces by |
| 430 |
> |
Vlugt {\it et al.}\cite{vlugt:cpc2007154} They fitted an effective |
| 431 |
> |
Lennard-Jones form of potential parameters for the interaction between |
| 432 |
> |
Au and pseudo-atoms CH$_x$ and S based on a well-established and |
| 433 |
> |
widely-used effective potential of Hautman and Klein for the Au(111) |
| 434 |
> |
surface.\cite{hautman:4994} As our simulations require the gold slab |
| 435 |
> |
to be flexible to accommodate thermal excitation, the pair-wise form |
| 436 |
> |
of potentials they developed was used for our study. |
| 437 |
|
|
| 438 |
< |
The results (Table \ref{AuThiolToluene}) show a |
| 439 |
< |
significant conductance enhancement compared to the gold/water |
| 440 |
< |
interface without capping agent and agree with available experimental |
| 441 |
< |
data. This indicates that the metal-metal potential, though not |
| 442 |
< |
predicting an accurate bulk metal thermal conductivity, does not |
| 443 |
< |
greatly interfere with the simulation of the thermal conductance |
| 444 |
< |
behavior across a non-metal interface. The solvent model is not |
| 445 |
< |
particularly volatile, so the simulation cell does not expand |
| 446 |
< |
significantly under higher temperature. We did not observe a |
| 447 |
< |
significant conductance decrease when the temperature was increased to |
| 448 |
< |
300K. The results show that the two definitions used for $G$ yield |
| 335 |
< |
comparable values, though $G^\prime$ tends to be smaller. |
| 438 |
> |
The potentials developed from {\it ab initio} calculations by Leng |
| 439 |
> |
{\it et al.}\cite{doi:10.1021/jp034405s} are adopted for the |
| 440 |
> |
interactions between Au and aromatic C/H atoms in toluene. However, |
| 441 |
> |
the Lennard-Jones parameters between Au and other types of particles, |
| 442 |
> |
(e.g. AA alkanes) have not yet been established. For these |
| 443 |
> |
interactions, the Lorentz-Berthelot mixing rule can be used to derive |
| 444 |
> |
effective single-atom LJ parameters for the metal using the fit values |
| 445 |
> |
for toluene. These are then used to construct reasonable mixing |
| 446 |
> |
parameters for the interactions between the gold and other atoms. |
| 447 |
> |
Table \ref{MnM} summarizes the ``metal/non-metal'' parameters used in |
| 448 |
> |
our simulations. |
| 449 |
|
|
| 450 |
|
\begin{table*} |
| 451 |
|
\begin{minipage}{\linewidth} |
| 452 |
|
\begin{center} |
| 453 |
< |
\caption{Computed interfacial thermal conductivity ($G$ and |
| 454 |
< |
$G^\prime$) values for the Au/butanethiol/toluene interface at |
| 455 |
< |
different temperatures using a range of energy fluxes.} |
| 456 |
< |
|
| 344 |
< |
\begin{tabular}{cccc} |
| 453 |
> |
\caption{Non-bonded interaction parameters (including cross |
| 454 |
> |
interactions with Au atoms) for both force fields used in this |
| 455 |
> |
work.} |
| 456 |
> |
\begin{tabular}{lllllll} |
| 457 |
|
\hline\hline |
| 458 |
< |
$\langle T\rangle$ & $J_z$ & $G$ & $G^\prime$ \\ |
| 459 |
< |
(K) & (GW/m$^2$) & \multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
| 458 |
> |
& Site & $\sigma_{ii}$ & $\epsilon_{ii}$ & $q_i$ & |
| 459 |
> |
$\sigma_{Au-i}$ & $\epsilon_{Au-i}$ \\ |
| 460 |
> |
& & (\AA) & (kcal/mol) & ($e$) & (\AA) & (kcal/mol) \\ |
| 461 |
|
\hline |
| 462 |
< |
200 & 1.86 & 180 & 135 \\ |
| 463 |
< |
& 2.15 & 204 & 113 \\ |
| 464 |
< |
& 3.93 & 175 & 114 \\ |
| 465 |
< |
300 & 1.91 & 143 & 125 \\ |
| 466 |
< |
& 4.19 & 134 & 113 \\ |
| 462 |
> |
United Atom (UA) |
| 463 |
> |
&CH3 & 3.75 & 0.1947 & - & 3.54 & 0.2146 \\ |
| 464 |
> |
&CH2 & 3.95 & 0.0914 & - & 3.54 & 0.1749 \\ |
| 465 |
> |
&CHar & 3.695 & 0.1003 & - & 3.4625 & 0.1680 \\ |
| 466 |
> |
&CRar & 3.88 & 0.04173 & - & 3.555 & 0.1604 \\ |
| 467 |
> |
\hline |
| 468 |
> |
All Atom (AA) |
| 469 |
> |
&CT3 & 3.50 & 0.066 & -0.18 & 3.365 & 0.1373 \\ |
| 470 |
> |
&CT2 & 3.50 & 0.066 & -0.12 & 3.365 & 0.1373 \\ |
| 471 |
> |
&CTT & 3.50 & 0.066 & -0.065 & 3.365 & 0.1373 \\ |
| 472 |
> |
&HC & 2.50 & 0.030 & 0.06 & 2.865 & 0.09256 \\ |
| 473 |
> |
&CA & 3.55 & 0.070 & -0.115 & 3.173 & 0.0640 \\ |
| 474 |
> |
&HA & 2.42 & 0.030 & 0.115 & 2.746 & 0.0414 \\ |
| 475 |
> |
\hline |
| 476 |
> |
Both UA and AA |
| 477 |
> |
& S & 4.45 & 0.25 & - & 2.40 & 8.465 \\ |
| 478 |
|
\hline\hline |
| 479 |
|
\end{tabular} |
| 480 |
< |
\label{AuThiolToluene} |
| 480 |
> |
\label{MnM} |
| 481 |
|
\end{center} |
| 482 |
|
\end{minipage} |
| 483 |
|
\end{table*} |
| 484 |
|
|
| 361 |
– |
\subsection{Hexane Solvent} |
| 485 |
|
|
| 486 |
< |
Using the united-atom model, different coverages of capping agent, |
| 487 |
< |
temperatures of simulations and numbers of solvent molecules were all |
| 488 |
< |
investigated and Table \ref{AuThiolHexaneUA} shows the results of |
| 489 |
< |
these computations. The number of hexane molecules in our simulations |
| 490 |
< |
does not affect the calculations significantly. However, a very long |
| 491 |
< |
length scale for the thermal gradient axis ($z$) may cause excessively |
| 492 |
< |
hot or cold temperatures in the middle of the solvent region and lead |
| 493 |
< |
to undesired phenomena such as solvent boiling or freezing, while too |
| 371 |
< |
few solvent molecules would change the normal behavior of the liquid |
| 372 |
< |
phase. Our $N_{hexane}$ values were chosen to ensure that these |
| 373 |
< |
extreme cases did not happen to our simulations. |
| 374 |
< |
|
| 375 |
< |
Table \ref{AuThiolHexaneUA} enables direct comparison between |
| 376 |
< |
different coverages of capping agent, when other system parameters are |
| 377 |
< |
held constant. With high coverage of butanethiol on the gold surface, |
| 378 |
< |
the interfacial thermal conductance is enhanced |
| 379 |
< |
significantly. Interestingly, a slightly lower butanethiol coverage |
| 380 |
< |
leads to a moderately higher conductivity. This is probably due to |
| 381 |
< |
more solvent/capping agent contact when butanethiol molecules are |
| 382 |
< |
not densely packed, which enhances the interactions between the two |
| 383 |
< |
phases and lowers the thermal transfer barrier of this interface. |
| 384 |
< |
% [COMPARE TO AU/WATER IN PAPER] |
| 486 |
> |
\section{Results} |
| 487 |
> |
There are many factors contributing to the measured interfacial |
| 488 |
> |
conductance; some of these factors are physically motivated |
| 489 |
> |
(e.g. coverage of the surface by the capping agent coverage and |
| 490 |
> |
solvent identity), while some are governed by parameters of the |
| 491 |
> |
methodology (e.g. applied flux and the formulas used to obtain the |
| 492 |
> |
conductance). In this section we discuss the major physical and |
| 493 |
> |
calculational effects on the computed conductivity. |
| 494 |
|
|
| 495 |
< |
It is also noted that the overall simulation temperature is another |
| 387 |
< |
factor that affects the interfacial thermal conductance. One |
| 388 |
< |
possibility of this effect may be rooted in the decrease in density of |
| 389 |
< |
the liquid phase. We observed that when the average temperature |
| 390 |
< |
increases from 200K to 250K, the bulk hexane density becomes lower |
| 391 |
< |
than experimental value, as the system is equilibrated under NPT |
| 392 |
< |
ensemble. This leads to lower contact between solvent and capping |
| 393 |
< |
agent, and thus lower conductivity. |
| 495 |
> |
\subsection{Effects due to capping agent coverage} |
| 496 |
|
|
| 497 |
< |
Conductivity values are more difficult to obtain under higher |
| 498 |
< |
temperatures. This is because the Au surface tends to undergo |
| 499 |
< |
reconstructions in relatively high temperatures. Surface Au atoms can |
| 500 |
< |
migrate outward to reach higher Au-S contact; and capping agent |
| 501 |
< |
molecules can be embedded into the surface Au layer due to the same |
| 502 |
< |
driving force. This phenomenon agrees with experimental |
| 401 |
< |
results\cite{doi:10.1021/j100035a033,doi:10.1021/la026493y}. A surface |
| 402 |
< |
fully covered in capping agent is more susceptible to reconstruction, |
| 403 |
< |
possibly because fully coverage prevents other means of capping agent |
| 404 |
< |
relaxation, such as migration to an empty neighbor three-fold site. |
| 497 |
> |
A series of different initial conditions with a range of surface |
| 498 |
> |
coverages was prepared and solvated with various with both of the |
| 499 |
> |
solvent molecules. These systems were then equilibrated and their |
| 500 |
> |
interfacial thermal conductivity was measured with the NIVS |
| 501 |
> |
algorithm. Figure \ref{coverage} demonstrates the trend of conductance |
| 502 |
> |
with respect to surface coverage. |
| 503 |
|
|
| 504 |
< |
%MAY ADD MORE DATA TO TABLE |
| 504 |
> |
\begin{figure} |
| 505 |
> |
\includegraphics[width=\linewidth]{coverage} |
| 506 |
> |
\caption{Comparison of interfacial thermal conductivity ($G$) values |
| 507 |
> |
for the Au-butanethiol/solvent interface with various UA models and |
| 508 |
> |
different capping agent coverages at $\langle T\rangle\sim$200K.} |
| 509 |
> |
\label{coverage} |
| 510 |
> |
\end{figure} |
| 511 |
> |
|
| 512 |
> |
In partially covered surfaces, the derivative definition for |
| 513 |
> |
$G^\prime$ (Eq. \ref{derivativeG}) becomes difficult to apply, as the |
| 514 |
> |
location of maximum change of $\lambda$ becomes washed out. The |
| 515 |
> |
discrete definition (Eq. \ref{discreteG}) is easier to apply, as the |
| 516 |
> |
Gibbs dividing surface is still well-defined. Therefore, $G$ (not |
| 517 |
> |
$G^\prime$) was used in this section. |
| 518 |
> |
|
| 519 |
> |
From Figure \ref{coverage}, one can see the significance of the |
| 520 |
> |
presence of capping agents. When even a small fraction of the Au(111) |
| 521 |
> |
surface sites are covered with butanethiols, the conductivity exhibits |
| 522 |
> |
an enhancement by at least a factor of 3. Cappping agents are clearly |
| 523 |
> |
playing a major role in thermal transport at metal / organic solvent |
| 524 |
> |
surfaces. |
| 525 |
> |
|
| 526 |
> |
We note a non-monotonic behavior in the interfacial conductance as a |
| 527 |
> |
function of surface coverage. The maximum conductance (largest $G$) |
| 528 |
> |
happens when the surfaces are about 75\% covered with butanethiol |
| 529 |
> |
caps. The reason for this behavior is not entirely clear. One |
| 530 |
> |
explanation is that incomplete butanethiol coverage allows small gaps |
| 531 |
> |
between butanethiols to form. These gaps can be filled by transient |
| 532 |
> |
solvent molecules. These solvent molecules couple very strongly with |
| 533 |
> |
the hot capping agent molecules near the surface, and can then carry |
| 534 |
> |
away (diffusively) the excess thermal energy from the surface. |
| 535 |
> |
|
| 536 |
> |
There appears to be a competition between the conduction of the |
| 537 |
> |
thermal energy away from the surface by the capping agents (enhanced |
| 538 |
> |
by greater coverage) and the coupling of the capping agents with the |
| 539 |
> |
solvent (enhanced by interdigitation at lower coverages). This |
| 540 |
> |
competition would lead to the non-monotonic coverage behavior observed |
| 541 |
> |
here. |
| 542 |
> |
|
| 543 |
> |
Results for rigid body toluene solvent, as well as the UA hexane, are |
| 544 |
> |
within the ranges expected from prior experimental |
| 545 |
> |
work.\cite{Wilson:2002uq,cahill:793,PhysRevB.80.195406} This suggests |
| 546 |
> |
that explicit hydrogen atoms might not be required for modeling |
| 547 |
> |
thermal transport in these systems. C-H vibrational modes do not see |
| 548 |
> |
significant excited state population at low temperatures, and are not |
| 549 |
> |
likely to carry lower frequency excitations from the solid layer into |
| 550 |
> |
the bulk liquid. |
| 551 |
> |
|
| 552 |
> |
The toluene solvent does not exhibit the same behavior as hexane in |
| 553 |
> |
that $G$ remains at approximately the same magnitude when the capping |
| 554 |
> |
coverage increases from 25\% to 75\%. Toluene, as a rigid planar |
| 555 |
> |
molecule, cannot occupy the relatively small gaps between the capping |
| 556 |
> |
agents as easily as the chain-like {\it n}-hexane. The effect of |
| 557 |
> |
solvent coupling to the capping agent is therefore weaker in toluene |
| 558 |
> |
except at the very lowest coverage levels. This effect counters the |
| 559 |
> |
coverage-dependent conduction of heat away from the metal surface, |
| 560 |
> |
leading to a much flatter $G$ vs. coverage trend than is observed in |
| 561 |
> |
{\it n}-hexane. |
| 562 |
> |
|
| 563 |
> |
\subsection{Effects due to Solvent \& Solvent Models} |
| 564 |
> |
In addition to UA solvent and capping agent models, AA models have |
| 565 |
> |
also been included in our simulations. In most of this work, the same |
| 566 |
> |
(UA or AA) model for solvent and capping agent was used, but it is |
| 567 |
> |
also possible to utilize different models for different components. |
| 568 |
> |
We have also included isotopic substitutions (Hydrogen to Deuterium) |
| 569 |
> |
to decrease the explicit vibrational overlap between solvent and |
| 570 |
> |
capping agent. Table \ref{modelTest} summarizes the results of these |
| 571 |
> |
studies. |
| 572 |
> |
|
| 573 |
|
\begin{table*} |
| 574 |
|
\begin{minipage}{\linewidth} |
| 575 |
|
\begin{center} |
| 410 |
– |
\caption{Computed interfacial thermal conductivity ($G$ and |
| 411 |
– |
$G^\prime$) values for the Au/butanethiol/hexane interface |
| 412 |
– |
with united-atom model and different capping agent coverage |
| 413 |
– |
and solvent molecule numbers at different temperatures using a |
| 414 |
– |
range of energy fluxes.} |
| 576 |
|
|
| 577 |
< |
\begin{tabular}{cccccc} |
| 577 |
> |
\caption{Computed interfacial thermal conductance ($G$ and |
| 578 |
> |
$G^\prime$) values for interfaces using various models for |
| 579 |
> |
solvent and capping agent (or without capping agent) at |
| 580 |
> |
$\langle T\rangle\sim$200K. (D stands for deuterated solvent |
| 581 |
> |
or capping agent molecules; ``Avg.'' denotes results that are |
| 582 |
> |
averages of simulations under different applied thermal flux values $(J_z)$. Error |
| 583 |
> |
estimates are indicated in parentheses.)} |
| 584 |
> |
|
| 585 |
> |
\begin{tabular}{llccc} |
| 586 |
|
\hline\hline |
| 587 |
< |
Thiol & $\langle T\rangle$ & & $J_z$ & $G$ & $G^\prime$ \\ |
| 588 |
< |
coverage (\%) & (K) & $N_{hexane}$ & (GW/m$^2$) & |
| 587 |
> |
Butanethiol model & Solvent & $J_z$ & $G$ & $G^\prime$ \\ |
| 588 |
> |
(or bare surface) & model & (GW/m$^2$) & |
| 589 |
|
\multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
| 590 |
|
\hline |
| 591 |
< |
0.0 & 200 & 200 & 0.96 & 43.3 & 42.7 \\ |
| 592 |
< |
& & & 1.91 & 45.7 & 42.9 \\ |
| 593 |
< |
& & 166 & 0.96 & 43.1 & 53.4 \\ |
| 594 |
< |
88.9 & 200 & 166 & 1.94 & 172 & 108 \\ |
| 595 |
< |
100.0 & 250 & 200 & 0.96 & 81.8 & 67.0 \\ |
| 596 |
< |
& & 166 & 0.98 & 79.0 & 62.9 \\ |
| 597 |
< |
& & & 1.44 & 76.2 & 64.8 \\ |
| 598 |
< |
& 200 & 200 & 1.92 & 129 & 87.3 \\ |
| 599 |
< |
& & & 1.93 & 131 & 77.5 \\ |
| 600 |
< |
& & 166 & 0.97 & 115 & 69.3 \\ |
| 601 |
< |
& & & 1.94 & 125 & 87.1 \\ |
| 591 |
> |
UA & UA hexane & Avg. & 131(9) & 87(10) \\ |
| 592 |
> |
& UA hexane(D) & 1.95 & 153(5) & 136(13) \\ |
| 593 |
> |
& AA hexane & Avg. & 131(6) & 122(10) \\ |
| 594 |
> |
& UA toluene & 1.96 & 187(16) & 151(11) \\ |
| 595 |
> |
& AA toluene & 1.89 & 200(36) & 149(53) \\ |
| 596 |
> |
\hline |
| 597 |
> |
AA & UA hexane & 1.94 & 116(9) & 129(8) \\ |
| 598 |
> |
& AA hexane & Avg. & 442(14) & 356(31) \\ |
| 599 |
> |
& AA hexane(D) & 1.93 & 222(12) & 234(54) \\ |
| 600 |
> |
& UA toluene & 1.98 & 125(25) & 97(60) \\ |
| 601 |
> |
& AA toluene & 3.79 & 487(56) & 290(42) \\ |
| 602 |
> |
\hline |
| 603 |
> |
AA(D) & UA hexane & 1.94 & 158(25) & 172(4) \\ |
| 604 |
> |
& AA hexane & 1.92 & 243(29) & 191(11) \\ |
| 605 |
> |
& AA toluene & 1.93 & 364(36) & 322(67) \\ |
| 606 |
> |
\hline |
| 607 |
> |
bare & UA hexane & Avg. & 46.5(3.2) & 49.4(4.5) \\ |
| 608 |
> |
& UA hexane(D) & 0.98 & 43.9(4.6) & 43.0(2.0) \\ |
| 609 |
> |
& AA hexane & 0.96 & 31.0(1.4) & 29.4(1.3) \\ |
| 610 |
> |
& UA toluene & 1.99 & 70.1(1.3) & 65.8(0.5) \\ |
| 611 |
|
\hline\hline |
| 612 |
|
\end{tabular} |
| 613 |
< |
\label{AuThiolHexaneUA} |
| 613 |
> |
\label{modelTest} |
| 614 |
|
\end{center} |
| 615 |
|
\end{minipage} |
| 616 |
|
\end{table*} |
| 617 |
|
|
| 618 |
< |
For the all-atom model, the liquid hexane phase was not stable under NPT |
| 619 |
< |
conditions. Therefore, the simulation length scale parameters are |
| 620 |
< |
adopted from previous equilibration results of the united-atom model |
| 443 |
< |
at 200K. Table \ref{AuThiolHexaneAA} shows the results of these |
| 444 |
< |
simulations. The conductivity values calculated with full capping |
| 445 |
< |
agent coverage are substantially larger than observed in the |
| 446 |
< |
united-atom model, and is even higher than predicted by |
| 447 |
< |
experiments. It is possible that our parameters for metal-non-metal |
| 448 |
< |
particle interactions lead to an overestimate of the interfacial |
| 449 |
< |
thermal conductivity, although the active C-H vibrations in the |
| 450 |
< |
all-atom model (which should not be appreciably populated at normal |
| 451 |
< |
temperatures) could also account for this high conductivity. The major |
| 452 |
< |
thermal transfer barrier of Au/butanethiol/hexane interface is between |
| 453 |
< |
the liquid phase and the capping agent, so extra degrees of freedom |
| 454 |
< |
such as the C-H vibrations could enhance heat exchange between these |
| 455 |
< |
two phases and result in a much higher conductivity. |
| 618 |
> |
To facilitate direct comparison between force fields, systems with the |
| 619 |
> |
same capping agent and solvent were prepared with the same length |
| 620 |
> |
scales for the simulation cells. |
| 621 |
|
|
| 622 |
+ |
On bare metal / solvent surfaces, different force field models for |
| 623 |
+ |
hexane yield similar results for both $G$ and $G^\prime$, and these |
| 624 |
+ |
two definitions agree with each other very well. This is primarily an |
| 625 |
+ |
indicator of weak interactions between the metal and the solvent, and |
| 626 |
+ |
is a typical case for acoustic impedance mismatch between these two |
| 627 |
+ |
phases. |
| 628 |
+ |
|
| 629 |
+ |
For the fully-covered surfaces, the choice of force field for the |
| 630 |
+ |
capping agent and solvent has a large impact on the calulated values |
| 631 |
+ |
of $G$ and $G^\prime$. The AA thiol to AA solvent conductivities are |
| 632 |
+ |
much larger than their UA to UA counterparts, and these values exceed |
| 633 |
+ |
the experimental estimates by a large measure. The AA force field |
| 634 |
+ |
allows significant energy to go into C-H (or C-D) stretching modes, |
| 635 |
+ |
and since these modes are high frequency, this non-quantum behavior is |
| 636 |
+ |
likely responsible for the overestimate of the conductivity. Compared |
| 637 |
+ |
to the AA model, the UA model yields more reasonable conductivity |
| 638 |
+ |
values with much higher computational efficiency. |
| 639 |
+ |
|
| 640 |
+ |
\subsubsection{Are electronic excitations in the metal important?} |
| 641 |
+ |
Because they lack electronic excitations, the QSC and related embedded |
| 642 |
+ |
atom method (EAM) models for gold are known to predict unreasonably |
| 643 |
+ |
low values for bulk conductivity |
| 644 |
+ |
($\lambda$).\cite{kuang:164101,ISI:000207079300006,Clancy:1992} If the |
| 645 |
+ |
conductance between the phases ($G$) is governed primarily by phonon |
| 646 |
+ |
excitation (and not electronic degrees of freedom), one would expect a |
| 647 |
+ |
classical model to capture most of the interfacial thermal |
| 648 |
+ |
conductance. Our results for $G$ and $G^\prime$ indicate that this is |
| 649 |
+ |
indeed the case, and suggest that the modeling of interfacial thermal |
| 650 |
+ |
transport depends primarily on the description of the interactions |
| 651 |
+ |
between the various components at the interface. When the metal is |
| 652 |
+ |
chemically capped, the primary barrier to thermal conductivity appears |
| 653 |
+ |
to be the interface between the capping agent and the surrounding |
| 654 |
+ |
solvent, so the excitations in the metal have little impact on the |
| 655 |
+ |
value of $G$. |
| 656 |
+ |
|
| 657 |
+ |
\subsection{Effects due to methodology and simulation parameters} |
| 658 |
+ |
|
| 659 |
+ |
We have varied the parameters of the simulations in order to |
| 660 |
+ |
investigate how these factors would affect the computation of $G$. Of |
| 661 |
+ |
particular interest are: 1) the length scale for the applied thermal |
| 662 |
+ |
gradient (modified by increasing the amount of solvent in the system), |
| 663 |
+ |
2) the sign and magnitude of the applied thermal flux, 3) the average |
| 664 |
+ |
temperature of the simulation (which alters the solvent density during |
| 665 |
+ |
equilibration), and 4) the definition of the interfacial conductance |
| 666 |
+ |
(Eqs. (\ref{discreteG}) or (\ref{derivativeG})) used in the |
| 667 |
+ |
calculation. |
| 668 |
+ |
|
| 669 |
+ |
Systems of different lengths were prepared by altering the number of |
| 670 |
+ |
solvent molecules and extending the length of the box along the $z$ |
| 671 |
+ |
axis to accomodate the extra solvent. Equilibration at the same |
| 672 |
+ |
temperature and pressure conditions led to nearly identical surface |
| 673 |
+ |
areas ($L_x$ and $L_y$) available to the metal and capping agent, |
| 674 |
+ |
while the extra solvent served mainly to lengthen the axis that was |
| 675 |
+ |
used to apply the thermal flux. For a given value of the applied |
| 676 |
+ |
flux, the different $z$ length scale has only a weak effect on the |
| 677 |
+ |
computed conductivities (Table \ref{AuThiolHexaneUA}). |
| 678 |
+ |
|
| 679 |
+ |
\subsubsection{Effects of applied flux} |
| 680 |
+ |
The NIVS algorithm allows changes in both the sign and magnitude of |
| 681 |
+ |
the applied flux. It is possible to reverse the direction of heat |
| 682 |
+ |
flow simply by changing the sign of the flux, and thermal gradients |
| 683 |
+ |
which would be difficult to obtain experimentally ($5$ K/\AA) can be |
| 684 |
+ |
easily simulated. However, the magnitude of the applied flux is not |
| 685 |
+ |
arbitary if one aims to obtain a stable and reliable thermal gradient. |
| 686 |
+ |
A temperature gradient can be lost in the noise if $|J_z|$ is too |
| 687 |
+ |
small, and excessive $|J_z|$ values can cause phase transitions if the |
| 688 |
+ |
extremes of the simulation cell become widely separated in |
| 689 |
+ |
temperature. Also, if $|J_z|$ is too large for the bulk conductivity |
| 690 |
+ |
of the materials, the thermal gradient will never reach a stable |
| 691 |
+ |
state. |
| 692 |
+ |
|
| 693 |
+ |
Within a reasonable range of $J_z$ values, we were able to study how |
| 694 |
+ |
$G$ changes as a function of this flux. In what follows, we use |
| 695 |
+ |
positive $J_z$ values to denote the case where energy is being |
| 696 |
+ |
transferred by the method from the metal phase and into the liquid. |
| 697 |
+ |
The resulting gradient therefore has a higher temperature in the |
| 698 |
+ |
liquid phase. Negative flux values reverse this transfer, and result |
| 699 |
+ |
in higher temperature metal phases. The conductance measured under |
| 700 |
+ |
different applied $J_z$ values is listed in Tables |
| 701 |
+ |
\ref{AuThiolHexaneUA} and \ref{AuThiolToluene}. These results do not |
| 702 |
+ |
indicate that $G$ depends strongly on $J_z$ within this flux |
| 703 |
+ |
range. The linear response of flux to thermal gradient simplifies our |
| 704 |
+ |
investigations in that we can rely on $G$ measurement with only a |
| 705 |
+ |
small number $J_z$ values. |
| 706 |
+ |
|
| 707 |
|
\begin{table*} |
| 708 |
|
\begin{minipage}{\linewidth} |
| 709 |
|
\begin{center} |
| 460 |
– |
|
| 710 |
|
\caption{Computed interfacial thermal conductivity ($G$ and |
| 711 |
< |
$G^\prime$) values for the Au/butanethiol/hexane interface |
| 712 |
< |
with all-atom model and different capping agent coverage at |
| 713 |
< |
200K using a range of energy fluxes.} |
| 711 |
> |
$G^\prime$) values for the 100\% covered Au-butanethiol/hexane |
| 712 |
> |
interfaces with UA model and different hexane molecule numbers |
| 713 |
> |
at different temperatures using a range of energy |
| 714 |
> |
fluxes. Error estimates indicated in parenthesis.} |
| 715 |
|
|
| 716 |
< |
\begin{tabular}{cccc} |
| 716 |
> |
\begin{tabular}{ccccccc} |
| 717 |
|
\hline\hline |
| 718 |
< |
Thiol & $J_z$ & $G$ & $G^\prime$ \\ |
| 719 |
< |
coverage (\%) & (GW/m$^2$) & \multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
| 718 |
> |
$\langle T\rangle$ & $N_{hexane}$ & $\rho_{hexane}$ & |
| 719 |
> |
$J_z$ & $G$ & $G^\prime$ \\ |
| 720 |
> |
(K) & & (g/cm$^3$) & (GW/m$^2$) & |
| 721 |
> |
\multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
| 722 |
|
\hline |
| 723 |
< |
0.0 & 0.95 & 28.5 & 27.2 \\ |
| 724 |
< |
& 1.88 & 30.3 & 28.9 \\ |
| 725 |
< |
100.0 & 2.87 & 551 & 294 \\ |
| 726 |
< |
& 3.81 & 494 & 193 \\ |
| 723 |
> |
200 & 266 & 0.672 & -0.96 & 102(3) & 80.0(0.8) \\ |
| 724 |
> |
& 200 & 0.688 & 0.96 & 125(16) & 90.2(15) \\ |
| 725 |
> |
& & & 1.91 & 139(10) & 101(10) \\ |
| 726 |
> |
& & & 2.83 & 141(6) & 89.9(9.8) \\ |
| 727 |
> |
& 166 & 0.681 & 0.97 & 141(30) & 78(22) \\ |
| 728 |
> |
& & & 1.92 & 138(4) & 98.9(9.5) \\ |
| 729 |
> |
\hline |
| 730 |
> |
250 & 200 & 0.560 & 0.96 & 75(10) & 61.8(7.3) \\ |
| 731 |
> |
& & & -0.95 & 49.4(0.3) & 45.7(2.1) \\ |
| 732 |
> |
& 166 & 0.569 & 0.97 & 80.3(0.6) & 67(11) \\ |
| 733 |
> |
& & & 1.44 & 76.2(5.0) & 64.8(3.8) \\ |
| 734 |
> |
& & & -0.95 & 56.4(2.5) & 54.4(1.1) \\ |
| 735 |
> |
& & & -1.85 & 47.8(1.1) & 53.5(1.5) \\ |
| 736 |
|
\hline\hline |
| 737 |
|
\end{tabular} |
| 738 |
< |
\label{AuThiolHexaneAA} |
| 738 |
> |
\label{AuThiolHexaneUA} |
| 739 |
|
\end{center} |
| 740 |
|
\end{minipage} |
| 741 |
|
\end{table*} |
| 742 |
|
|
| 743 |
< |
%subsubsection{Vibrational spectrum study on conductance mechanism} |
| 744 |
< |
To investigate the mechanism of this interfacial thermal conductance, |
| 745 |
< |
the vibrational spectra of various gold systems were obtained and are |
| 746 |
< |
shown as in the upper panel of Fig. \ref{vibration}. To obtain these |
| 747 |
< |
spectra, one first runs a simulation in the NVE ensemble and collects |
| 748 |
< |
snapshots of configurations; these configurations are used to compute |
| 749 |
< |
the velocity auto-correlation functions, which is used to construct a |
| 750 |
< |
power spectrum via a Fourier transform. The gold surfaces covered by |
| 751 |
< |
butanethiol molecules exhibit an additional peak observed at a |
| 491 |
< |
frequency of $\sim$170cm$^{-1}$, which is attributed to the vibration |
| 492 |
< |
of the S-Au bond. This vibration enables efficient thermal transport |
| 493 |
< |
from surface Au atoms to the capping agents. Simultaneously, as shown |
| 494 |
< |
in the lower panel of Fig. \ref{vibration}, the large overlap of the |
| 495 |
< |
vibration spectra of butanethiol and hexane in the all-atom model, |
| 496 |
< |
including the C-H vibration, also suggests high thermal exchange |
| 497 |
< |
efficiency. The combination of these two effects produces the drastic |
| 498 |
< |
interfacial thermal conductance enhancement in the all-atom model. |
| 743 |
> |
The sign of $J_z$ is a different matter, however, as this can alter |
| 744 |
> |
the temperature on the two sides of the interface. The average |
| 745 |
> |
temperature values reported are for the entire system, and not for the |
| 746 |
> |
liquid phase, so at a given $\langle T \rangle$, the system with |
| 747 |
> |
positive $J_z$ has a warmer liquid phase. This means that if the |
| 748 |
> |
liquid carries thermal energy via convective transport, {\it positive} |
| 749 |
> |
$J_z$ values will result in increased molecular motion on the liquid |
| 750 |
> |
side of the interface, and this will increase the measured |
| 751 |
> |
conductivity. |
| 752 |
|
|
| 753 |
+ |
\subsubsection{Effects due to average temperature} |
| 754 |
+ |
|
| 755 |
+ |
We also studied the effect of average system temperature on the |
| 756 |
+ |
interfacial conductance. The simulations are first equilibrated in |
| 757 |
+ |
the NPT ensemble at 1 atm. The TraPPE-UA model for hexane tends to |
| 758 |
+ |
predict a lower boiling point (and liquid state density) than |
| 759 |
+ |
experiments. This lower-density liquid phase leads to reduced contact |
| 760 |
+ |
between the hexane and butanethiol, and this accounts for our |
| 761 |
+ |
observation of lower conductance at higher temperatures as shown in |
| 762 |
+ |
Table \ref{AuThiolHexaneUA}. In raising the average temperature from |
| 763 |
+ |
200K to 250K, the density drop of ~20\% in the solvent phase leads to |
| 764 |
+ |
a ~65\% drop in the conductance. |
| 765 |
+ |
|
| 766 |
+ |
Similar behavior is observed in the TraPPE-UA model for toluene, |
| 767 |
+ |
although this model has better agreement with the experimental |
| 768 |
+ |
densities of toluene. The expansion of the toluene liquid phase is |
| 769 |
+ |
not as significant as that of the hexane (8.3\% over 100K), and this |
| 770 |
+ |
limits the effect to ~20\% drop in thermal conductivity (Table |
| 771 |
+ |
\ref{AuThiolToluene}). |
| 772 |
+ |
|
| 773 |
+ |
Although we have not mapped out the behavior at a large number of |
| 774 |
+ |
temperatures, is clear that there will be a strong temperature |
| 775 |
+ |
dependence in the interfacial conductance when the physical properties |
| 776 |
+ |
of one side of the interface (notably the density) change rapidly as a |
| 777 |
+ |
function of temperature. |
| 778 |
+ |
|
| 779 |
+ |
\begin{table*} |
| 780 |
+ |
\begin{minipage}{\linewidth} |
| 781 |
+ |
\begin{center} |
| 782 |
+ |
\caption{Computed interfacial thermal conductivity ($G$ and |
| 783 |
+ |
$G^\prime$) values for a 90\% coverage Au-butanethiol/toluene |
| 784 |
+ |
interface at different temperatures using a range of energy |
| 785 |
+ |
fluxes. Error estimates indicated in parenthesis.} |
| 786 |
+ |
|
| 787 |
+ |
\begin{tabular}{ccccc} |
| 788 |
+ |
\hline\hline |
| 789 |
+ |
$\langle T\rangle$ & $\rho_{toluene}$ & $J_z$ & $G$ & $G^\prime$ \\ |
| 790 |
+ |
(K) & (g/cm$^3$) & (GW/m$^2$) & \multicolumn{2}{c}{(MW/m$^2$/K)} \\ |
| 791 |
+ |
\hline |
| 792 |
+ |
200 & 0.933 & 2.15 & 204(12) & 113(12) \\ |
| 793 |
+ |
& & -1.86 & 180(3) & 135(21) \\ |
| 794 |
+ |
& & -3.93 & 176(5) & 113(12) \\ |
| 795 |
+ |
\hline |
| 796 |
+ |
300 & 0.855 & -1.91 & 143(5) & 125(2) \\ |
| 797 |
+ |
& & -4.19 & 135(9) & 113(12) \\ |
| 798 |
+ |
\hline\hline |
| 799 |
+ |
\end{tabular} |
| 800 |
+ |
\label{AuThiolToluene} |
| 801 |
+ |
\end{center} |
| 802 |
+ |
\end{minipage} |
| 803 |
+ |
\end{table*} |
| 804 |
+ |
|
| 805 |
+ |
Besides the lower interfacial thermal conductance, surfaces at |
| 806 |
+ |
relatively high temperatures are susceptible to reconstructions, |
| 807 |
+ |
particularly when butanethiols fully cover the Au(111) surface. These |
| 808 |
+ |
reconstructions include surface Au atoms which migrate outward to the |
| 809 |
+ |
S atom layer, and butanethiol molecules which embed into the surface |
| 810 |
+ |
Au layer. The driving force for this behavior is the strong Au-S |
| 811 |
+ |
interactions which are modeled here with a deep Lennard-Jones |
| 812 |
+ |
potential. This phenomenon agrees with reconstructions that have beeen |
| 813 |
+ |
experimentally |
| 814 |
+ |
observed.\cite{doi:10.1021/j100035a033,doi:10.1021/la026493y}. Vlugt |
| 815 |
+ |
{\it et al.} kept their Au(111) slab rigid so that their simulations |
| 816 |
+ |
could reach 300K without surface |
| 817 |
+ |
reconstructions.\cite{vlugt:cpc2007154} Since surface reconstructions |
| 818 |
+ |
blur the interface, the measurement of $G$ becomes more difficult to |
| 819 |
+ |
conduct at higher temperatures. For this reason, most of our |
| 820 |
+ |
measurements are undertaken at $\langle T\rangle\sim$200K where |
| 821 |
+ |
reconstruction is minimized. |
| 822 |
+ |
|
| 823 |
+ |
However, when the surface is not completely covered by butanethiols, |
| 824 |
+ |
the simulated system appears to be more resistent to the |
| 825 |
+ |
reconstruction. O ur Au / butanethiol / toluene system had the Au(111) |
| 826 |
+ |
surfaces 90\% covered by butanethiols, but did not see this above |
| 827 |
+ |
phenomena even at $\langle T\rangle\sim$300K. That said, we did |
| 828 |
+ |
observe butanethiols migrating to neighboring three-fold sites during |
| 829 |
+ |
a simulation. Since the interface persisted in these simulations, |
| 830 |
+ |
were able to obtain $G$'s for these interfaces even at a relatively |
| 831 |
+ |
high temperature without being affected by surface reconstructions. |
| 832 |
+ |
|
| 833 |
+ |
\section{Discussion} |
| 834 |
+ |
|
| 835 |
+ |
The primary result of this work is that the capping agent acts as an |
| 836 |
+ |
efficient thermal coupler between solid and solvent phases. One of |
| 837 |
+ |
the ways the capping agent can carry out this role is to down-shift |
| 838 |
+ |
between the phonon vibrations in the solid (which carry the heat from |
| 839 |
+ |
the gold) and the molecular vibrations in the liquid (which carry some |
| 840 |
+ |
of the heat in the solvent). |
| 841 |
+ |
|
| 842 |
+ |
To investigate the mechanism of interfacial thermal conductance, the |
| 843 |
+ |
vibrational power spectrum was computed. Power spectra were taken for |
| 844 |
+ |
individual components in different simulations. To obtain these |
| 845 |
+ |
spectra, simulations were run after equilibration in the |
| 846 |
+ |
microcanonical (NVE) ensemble and without a thermal |
| 847 |
+ |
gradient. Snapshots of configurations were collected at a frequency |
| 848 |
+ |
that is higher than that of the fastest vibrations occuring in the |
| 849 |
+ |
simulations. With these configurations, the velocity auto-correlation |
| 850 |
+ |
functions can be computed: |
| 851 |
+ |
\begin{equation} |
| 852 |
+ |
C_A (t) = \langle\vec{v}_A (t)\cdot\vec{v}_A (0)\rangle |
| 853 |
+ |
\label{vCorr} |
| 854 |
+ |
\end{equation} |
| 855 |
+ |
The power spectrum is constructed via a Fourier transform of the |
| 856 |
+ |
symmetrized velocity autocorrelation function, |
| 857 |
+ |
\begin{equation} |
| 858 |
+ |
\hat{f}(\omega) = |
| 859 |
+ |
\int_{-\infty}^{\infty} C_A (t) e^{-2\pi it\omega}\,dt |
| 860 |
+ |
\label{fourier} |
| 861 |
+ |
\end{equation} |
| 862 |
+ |
|
| 863 |
+ |
\subsection{The role of specific vibrations} |
| 864 |
+ |
The vibrational spectra for gold slabs in different environments are |
| 865 |
+ |
shown as in Figure \ref{specAu}. Regardless of the presence of |
| 866 |
+ |
solvent, the gold surfaces which are covered by butanethiol molecules |
| 867 |
+ |
exhibit an additional peak observed at a frequency of |
| 868 |
+ |
$\sim$170cm$^{-1}$. We attribute this peak to the S-Au bonding |
| 869 |
+ |
vibration. This vibration enables efficient thermal coupling of the |
| 870 |
+ |
surface Au layer to the capping agents. Therefore, in our simulations, |
| 871 |
+ |
the Au / S interfaces do not appear to be the primary barrier to |
| 872 |
+ |
thermal transport when compared with the butanethiol / solvent |
| 873 |
+ |
interfaces. |
| 874 |
+ |
|
| 875 |
|
\begin{figure} |
| 876 |
|
\includegraphics[width=\linewidth]{vibration} |
| 877 |
< |
\caption{Vibrational spectra obtained for gold in different |
| 878 |
< |
environments (upper panel) and for Au/thiol/hexane simulation in |
| 879 |
< |
all-atom model (lower panel).} |
| 880 |
< |
\label{vibration} |
| 877 |
> |
\caption{Vibrational power spectra for gold in different solvent |
| 878 |
> |
environments. The presence of the butanethiol capping molecules |
| 879 |
> |
adds a vibrational peak at $\sim$170cm$^{-1}$.} |
| 880 |
> |
\label{specAu} |
| 881 |
|
\end{figure} |
| 507 |
– |
% 600dpi, letter size. too large? |
| 882 |
|
|
| 883 |
+ |
Also in this figure, we show the vibrational power spectrum for the |
| 884 |
+ |
bound butanethiol molecules, which also exhibits the same |
| 885 |
+ |
$\sim$170cm$^{-1}$ peak. |
| 886 |
|
|
| 887 |
+ |
\subsection{Overlap of power spectra} |
| 888 |
+ |
A comparison of the results obtained from the two different organic |
| 889 |
+ |
solvents can also provide useful information of the interfacial |
| 890 |
+ |
thermal transport process. In particular, the vibrational overlap |
| 891 |
+ |
between the butanethiol and the organic solvents suggests a highly |
| 892 |
+ |
efficient thermal exchange between these components. Very high |
| 893 |
+ |
thermal conductivity was observed when AA models were used and C-H |
| 894 |
+ |
vibrations were treated classically. The presence of extra degrees of |
| 895 |
+ |
freedom in the AA force field yields higher heat exchange rates |
| 896 |
+ |
between the two phases and results in a much higher conductivity than |
| 897 |
+ |
in the UA force field. |
| 898 |
+ |
|
| 899 |
+ |
The similarity in the vibrational modes available to solvent and |
| 900 |
+ |
capping agent can be reduced by deuterating one of the two components |
| 901 |
+ |
(Fig. \ref{aahxntln}). Once either the hexanes or the butanethiols |
| 902 |
+ |
are deuterated, one can observe a significantly lower $G$ and |
| 903 |
+ |
$G^\prime$ values (Table \ref{modelTest}). |
| 904 |
+ |
|
| 905 |
+ |
\begin{figure} |
| 906 |
+ |
\includegraphics[width=\linewidth]{aahxntln} |
| 907 |
+ |
\caption{Spectra obtained for all-atom (AA) Au / butanethiol / solvent |
| 908 |
+ |
systems. When butanethiol is deuterated (lower left), its |
| 909 |
+ |
vibrational overlap with hexane decreases significantly. Since |
| 910 |
+ |
aromatic molecules and the butanethiol are vibrationally dissimilar, |
| 911 |
+ |
the change is not as dramatic when toluene is the solvent (right).} |
| 912 |
+ |
\label{aahxntln} |
| 913 |
+ |
\end{figure} |
| 914 |
+ |
|
| 915 |
+ |
For the Au / butanethiol / toluene interfaces, having the AA |
| 916 |
+ |
butanethiol deuterated did not yield a significant change in the |
| 917 |
+ |
measured conductance. Compared to the C-H vibrational overlap between |
| 918 |
+ |
hexane and butanethiol, both of which have alkyl chains, the overlap |
| 919 |
+ |
between toluene and butanethiol is not as significant and thus does |
| 920 |
+ |
not contribute as much to the heat exchange process. |
| 921 |
+ |
|
| 922 |
+ |
Previous observations of Zhang {\it et al.}\cite{hase:2010} indicate |
| 923 |
+ |
that the {\it intra}molecular heat transport due to alkylthiols is |
| 924 |
+ |
highly efficient. Combining our observations with those of Zhang {\it |
| 925 |
+ |
et al.}, it appears that butanethiol acts as a channel to expedite |
| 926 |
+ |
heat flow from the gold surface and into the alkyl chain. The |
| 927 |
+ |
acoustic impedance mismatch between the metal and the liquid phase can |
| 928 |
+ |
therefore be effectively reduced with the presence of suitable capping |
| 929 |
+ |
agents. |
| 930 |
+ |
|
| 931 |
+ |
Deuterated models in the UA force field did not decouple the thermal |
| 932 |
+ |
transport as well as in the AA force field. The UA models, even |
| 933 |
+ |
though they have eliminated the high frequency C-H vibrational |
| 934 |
+ |
overlap, still have significant overlap in the lower-frequency |
| 935 |
+ |
portions of the infrared spectra (Figure \ref{uahxnua}). Deuterating |
| 936 |
+ |
the UA models did not decouple the low frequency region enough to |
| 937 |
+ |
produce an observable difference for the results of $G$ (Table |
| 938 |
+ |
\ref{modelTest}). |
| 939 |
+ |
|
| 940 |
+ |
\begin{figure} |
| 941 |
+ |
\includegraphics[width=\linewidth]{uahxnua} |
| 942 |
+ |
\caption{Vibrational spectra obtained for normal (upper) and |
| 943 |
+ |
deuterated (lower) hexane in Au-butanethiol/hexane |
| 944 |
+ |
systems. Butanethiol spectra are shown as reference. Both hexane and |
| 945 |
+ |
butanethiol were using United-Atom models.} |
| 946 |
+ |
\label{uahxnua} |
| 947 |
+ |
\end{figure} |
| 948 |
+ |
|
| 949 |
+ |
\section{Conclusions} |
| 950 |
+ |
The NIVS algorithm has been applied to simulations of |
| 951 |
+ |
butanethiol-capped Au(111) surfaces in the presence of organic |
| 952 |
+ |
solvents. This algorithm allows the application of unphysical thermal |
| 953 |
+ |
flux to transfer heat between the metal and the liquid phase. With the |
| 954 |
+ |
flux applied, we were able to measure the corresponding thermal |
| 955 |
+ |
gradients and to obtain interfacial thermal conductivities. Under |
| 956 |
+ |
steady states, 2-3 ns trajectory simulations are sufficient for |
| 957 |
+ |
computation of this quantity. |
| 958 |
+ |
|
| 959 |
+ |
Our simulations have seen significant conductance enhancement in the |
| 960 |
+ |
presence of capping agent, compared with the bare gold / liquid |
| 961 |
+ |
interfaces. The acoustic impedance mismatch between the metal and the |
| 962 |
+ |
liquid phase is effectively eliminated by a chemically-bonded capping |
| 963 |
+ |
agent. Furthermore, the coverage precentage of the capping agent plays |
| 964 |
+ |
an important role in the interfacial thermal transport |
| 965 |
+ |
process. Moderately low coverages allow higher contact between capping |
| 966 |
+ |
agent and solvent, and thus could further enhance the heat transfer |
| 967 |
+ |
process, giving a non-monotonic behavior of conductance with |
| 968 |
+ |
increasing coverage. |
| 969 |
+ |
|
| 970 |
+ |
Our results, particularly using the UA models, agree well with |
| 971 |
+ |
available experimental data. The AA models tend to overestimate the |
| 972 |
+ |
interfacial thermal conductance in that the classically treated C-H |
| 973 |
+ |
vibrations become too easily populated. Compared to the AA models, the |
| 974 |
+ |
UA models have higher computational efficiency with satisfactory |
| 975 |
+ |
accuracy, and thus are preferable in modeling interfacial thermal |
| 976 |
+ |
transport. |
| 977 |
+ |
|
| 978 |
+ |
Of the two definitions for $G$, the discrete form |
| 979 |
+ |
(Eq. \ref{discreteG}) was easier to use and gives out relatively |
| 980 |
+ |
consistent results, while the derivative form (Eq. \ref{derivativeG}) |
| 981 |
+ |
is not as versatile. Although $G^\prime$ gives out comparable results |
| 982 |
+ |
and follows similar trend with $G$ when measuring close to fully |
| 983 |
+ |
covered or bare surfaces, the spatial resolution of $T$ profile |
| 984 |
+ |
required for the use of a derivative form is limited by the number of |
| 985 |
+ |
bins and the sampling required to obtain thermal gradient information. |
| 986 |
+ |
|
| 987 |
+ |
Vlugt {\it et al.} have investigated the surface thiol structures for |
| 988 |
+ |
nanocrystalline gold and pointed out that they differ from those of |
| 989 |
+ |
the Au(111) surface.\cite{landman:1998,vlugt:cpc2007154} This |
| 990 |
+ |
difference could also cause differences in the interfacial thermal |
| 991 |
+ |
transport behavior. To investigate this problem, one would need an |
| 992 |
+ |
effective method for applying thermal gradients in non-planar |
| 993 |
+ |
(i.e. spherical) geometries. |
| 994 |
+ |
|
| 995 |
|
\section{Acknowledgments} |
| 996 |
|
Support for this project was provided by the National Science |
| 997 |
|
Foundation under grant CHE-0848243. Computational time was provided by |
| 998 |
|
the Center for Research Computing (CRC) at the University of Notre |
| 999 |
< |
Dame. \newpage |
| 999 |
> |
Dame. |
| 1000 |
> |
\newpage |
| 1001 |
|
|
| 1002 |
|
\bibliography{interfacial} |
| 1003 |
|
|
